Coating and lithiation of inorganic oxidants by reaction with lithiated reductants

ABSTRACT

A method for producing conductive carbon coated particles of an at least partially lithiated electroactive core material comprises the step of premixing an oxidant electroactive material with a metallated reductant followed by chemically reacting the oxidant electroactive material with the metallated reductant, said reductant being a coating precursor, said metal being at least one alkaline and/or at least one alkaline earth metal, and said chemically reacting being performed under conditions allowing reduction and metallation of the electroactive material via insertion/intercalation of the alkaline metal cation(s) and/or the alkaline earth metal cation(s) and coating formation via a polymerisation reaction like polyanionic or radicalic polymerisation of the reductant.

This application claims priority from European Patent Application No.11195377.4 filed Dec. 22, 2011 and European Patent Application No.12157429.7 filed Feb. 29, 2012, the entire disclosure of which isincorporated herein by reference.

TECHNICAL FIELD

The present invention concerns conductive microparticles suitable forbeing used in electrodes of lithium ion batteries as well as methods forthe production of such miroparticles and electrodes.

BACKGROUND ART

The electroactive materials of electrodes of lithium ion batteriescomprise at least one transition metal providing exchangeable valenceelectrons, said material also allowing insertion and removal orintercalation and deintercalation, respectively, of alkaline metal ionsin order to keep neutrality of the material in case of exchange ofvalence electrons.

Some very interesting electroactive materials are not or not suficientlyconductive per se. Such materials are used in the form of microparticles(also termed microparticulate form) or nanoparticles (also termednanoparticulate form) and in combination with a conductive matrix.Additional improvement is obtained if the particles are conductivelycoated.

It is assumed that conductive coatings add to the structural integrityof the particels because of improved regularity of electric fielddistribution on the surface of the particles and therewith connectedimproved structural integrity. In addition, even if the electroactivematerial particles are partially disintegrated over an extended numberof cycles, the carbon coating proved advantageous. This may be due toencapsulation of the disintegrated particles and—if breaking apart—inpartially conductively coated fragments. Methods for providingmicroparticles with a conductive coating are known. The preferredcoating is a coating with carbonaceous material.

Carbon and carbonaceous materials are known as good electricalconductors and are already used to increase the electronic conductivityof electroactive materials. In general, carbon coating of oxidematerials is carried out using a pyrolysis process that forms a thinlayer of carbonaceous material such as pyrolitic graphite on the surfaceof particles provided that the electroactive core material issufficiently stable in reducing atmosphere (see U.S. Pat. No.6,962,266). According to U.S. Pat. No. 6,962,266, the carbonaceouscoating may be obtained through thermal decomposition or throughdehydrogenation, e.g. by partial oxidation of organic materials such ashydrocarbons and their derivatives like polycyclic aromatic moieties,sugars, carbon hydride and polymers. In some embodiments a lithium saltof carboxylic acids is used for simultaneous lithiation and pyrolyticcarbonatious coating formation.

However, the problem with the coatings of the state of the art is thatthe pyrolysis reaction is not well defined. During pyrolysis, thehydrocarbon or carboxylic acid deposits may release compounds indifferent stats of oxidation/reduction like hydrogen or water and carbonoxides or dioxides resulting in an inhomogeneous coating of not clearlydefined composition and possibly in affected EAMs.

Thus, there is still a need for high energy storage materials with agood conductive coating and a method for obtaining such materialspreferably in a one step reaction.

DISCLOSURE OF THE INVENTION

Hence, it is a general object of the invention to provide optimizedcoating methods and therewith obtainable optimized carbon coatedelectroactive particles with a coating having improved homogeneity andpurity.

Now, in order to implement these and still further objects of theinvention, which will become more readily apparent as the descriptionproceeds, the method for producing conductively coated particlescomprising an at least partially metallated electroactive core materialis manifested by comprising the steps of premixing an oxidantelectroactive material with a metallated reductant followed bychemically reacting the oxidant electroactive material with themetallated reductant, said reductant being a coating precursor, saidmetal being at least one alkaline and/or at least one alkaline earthmetal, and said chemically reacting being performed under conditionsallowing reduction and metallation of the electroactive material viainsertion/intercalation of the alkalinemetal cation(s) and/or thealkaline earth metal cation(s) and coating formation via apolymerisation reaction, like polyanionic or radicalic polymerisation,of the reductant.

The terms insertion and intercalation or deinsertion anddeintercalation, respectively are used interchangeably for bothcrystalline and amorphous materials.

A metal comprising compound is termed metallated.

Insertion or intercalation, respectively, of different alkaline and/oralkaline earth metals at the same time like Li and Na and/or K can leadto a more stable system. Thus the use of mixed metallated reductantslike Li_(2-x)Na_(x)C₂ (x≤1) and/or Li_(2-x)K_(x)C₂ (x≤1) is also ofinterest.

In one embodiment, the metallated reductant comprises or consists ofalkaline metal(s), wherein the alkaline metal(s) comprises at least 50%lithium, preferably at least 95% lithium, more preferred at least 99%lithium.

For sake of readability, in the following description lithium ismentioned although besides of lithium sodium and potassium may also bepresent, or alkaline earth metals alone or in combination with alkalinemetals.

The method of the present invention is a one step method that allowssimultaneous lithiation and coating of inorganic oxidants. The coatingis not limited to carbon although carbon is preferred but may e.g. alsobe a boron nitride or a carbon nitride coating. Other possible coatingscomprise CB_(x) from B═C═B⁴⁻ compounds like Li₄CB₂, CB_(x)N_(y) from alithium pyrazine precursor like Ca_(10-x)Li_(2x)(BN₂)₄(CBN)₂ (see alsoWO 2004/069768), (S_(y)N)_(x) from e.g. Li_(g)NS₃, (CH)_(x)(polyacetylene) for example form LiHC₂.

The conditions allowing reduction and lithiation comprise applyingenergy in the form of

-   -   heat    -   tribological energy like (ball) milling    -   ultrasound    -   microwave.

In preferred embodiments, the chemical reaction can be induced eithervia thermal treatment of via tribological treatment, e.g. by ballmilling.

Both methods lead to conductively coated particles comprising an atleast partially lithiated electroactive core material, but to differentcore materials. While heat treatment produces a crystalline at leastpartially lithiated electroactive core material, ball milling results inan almost amorphous at least partially lithiated electroactive corematerial. This difference in the at least partially lithiatedelectroactive core material, i.e. whether it is crystalline oramorphous, has a strong influence on the electrochemical behavior.

The reaction is a redox reaction of the form

M _(x)reductant+oxidant→M_(x)oxidant_(reduced)+reductant_(surface)(reductant_(oxidized))

In the following description, the electroactive material orelectroactive core material or oxidant is abbreviated as EAM and the atleast partially lithiated electroactive core material as LiEAM.

Different to pyrolysis, the carbon coating takes place via astoichiometric reaction according to the equation 1:

x Li₂C₂ +Oxidant

Li_(2x)Oxidant_(reduced)+2x C_(surface)

Boron nitride coating and lithiation of formally inorganic oxidants maybe obtained by reaction with Li₃BN₂ according to the following equation2:

x Li₃BN₂+Oxidant

Li_(3x)Oxidant_(reduced) +x BN_(surface) x/2 N₂

Carbon nitride coating and lithiation of formally inorganic oxidants maybe obtained by reaction with Li₂CN₂ according to the following equation3:

x Li₂CN₂+Oxid ant

Li_(2x)Oxidant_(reduced) +x CN_(2x-y) surface y/2 N₂

Possible Oxidants are:

Transition metal oxides MoO₃, MnO₂, LiMn₂O₄, V₂O₅ Hydrated transitionmetal oxides H₂V₃O₈ Transition metal oxynitrides NbNO Transition metalphosphates M_(X)(PO₄)_(y) (M = Fe, Co, Mn, Ni) Transition metal oxidesglasses Glasses containing V2O5 and MoO3 Elements S; Se; Si

The EAMs preferably are in the form of microparticles or evennanoparticles. Usually they have average diameters below 10 μm,preferably below 5 μm, more preferred below 1 μm and especially below500 nm, in particular they are nanoparticles having an average particlesize in the range of 5 to 500 nm, preferably in the range of 5 to 400nm, more preferred in the range of 20 to 300 nm.

Also the lithium providing reductants are preferably of small size. Forexample lithium carbide (Li₂C₂) after synthesis has a particle size of10 to 100 μm. Since an as small as possible particle size is assumed toimprove homogeneity of the coating, it is reduced in size, e.g. by ballmilling for 1 hour with 500 rpm, to end up with a homogeneous particlesize of 1-5 μm.

Particle sizes of <10 μm, preferably 100 nm to 5 μm, more preferred 0.5to 1.5 μm are generally preferred for all Li and coating providingreductants.

Although (as shown above) other than carbon coatings can be applied viathe inventive methods, carbon is presently preferred due to itsconductivity that is better than the one of CN and BN and because of thegood availability of suitable metallated precursors.

The invention is now further described for a carbon coating. However,the respective information is also applicable to other coatings.

Due to the stoichiometry of the reactions, the thickness of the coatingcan only be varied by variation of the particle size of the EAM or—forthinner coatings—by starting from an EAM that has already been partiallylithiated. For a carbon coating starting from Li₂C₂, the amount ofsurface carbon corresponds to the amount of lithium taken up by the EAM.Since big particles have a higher ratio between volume and surface, as arule the coating will be much thicker for big particles. The minimalthickness of 2 nm so far was observed for a 40 nm particle of LiFePO₄and a maximum thickness of 30 nm for a 5 μm large particle of LiV₂O₅. Itwas found that even the thick coating of 30 nm allowsintercalation/deintercalation, although at somewhat lower speed than athin coating. The minimal thickness of a coating is assumed to be below1 nm but presumably above 0.5 nm because the product deposited is notgraphene. In addition, it is also assumed that the coating is protectingthe EAM and therewith enhancing the cycle stability. Thus, the averagethickness of the coating is preferably between 0.5 to 30 nm, morepreferred between 0.5 to 2 nm.

Theoretically, the ideal thickness of the carbon coating is just thickenough to

-   -   prevent EAMs/LiEAMs from dissolving    -   prevent additional solid electrolyte interphases (SEI) growth of        interphases that are formed on e.g. the cathode due to catalytic        redox reactions of the electrolyte    -   install reasonable surface conductivity for Li-ions and        electrons    -   possibly even glue the particles together.

In any case, it was found that in most cases partial or completeintercalation of cathode materials during this process improves theirelectrochemical properties.

In view of the homogeneous coverage of the particles with the carbon,some migration of the carbon on the surface of the particles is assumed.

Irrespective of whether the reaction is performed by ball milling orheat treatment, the reactants preferably are carefully premixed, inorder to ensure that the reaction is started with homogeneously mixedstarting materials.

The whole reaction, also the premixing can and preferably is performedin the absence of any solvent thereby avoiding any solvent removal step.

In e.g. the ball milling procedure the reaction starts directly.Suitable reaction conditions for this tribochemical step are e.g. arotation speed of 200-1500 rpm during 15 to 45 minutes, such as around30 minutes or 30 minutes. Hitherto optimal products were obtained with400 rpm during 30 minutes. Also important is the ratio between theweight of the balls and the weight of the sample which with thepresently used equipment was found to be in the range from 6:1 to 4:1,preferably around 5:1 like 5.2:1 to 4.8:1.

With the exception of the weight ratio the material of the balls isirrelevant, provided that it is sufficiently hard. Examples of suitablematerials are: Agate, a modification of silica, steal, Cr₂O₃, and Al₂O₃

Since the reaction is only slightly exothermic, no raise of the overalltemperature is observed during ball milling such that the tribochemicalreaction is devoid of a thermal treatment.

The ball milling method therefore is also applicable for heat sensitivematerials as H₂V₃O₈ without risking decomposition.

The disadvantage of the ballmilling method is that the conditions aremore difficult to adjust and that therefore it is more difficult toavoid side reactions (see below).

The ball milling method results in an amorphous material.

Heat treatment can be performed with fast heating rate of for examplebetween 150 to 200 K/h like 180 K/h. In preferred embodiments, heattreatment is performed either with a slow heating rate or with highheating rate for an initial phase followed by a slow heating rate. Aslow heating rate of e.g. between 50 to 70 K/h should be applied forabout at least the last hour, i.e. starting at 50 to 70 K below thereaction temperature.

A presently preferred heating rate is around 60 K/h starting at about 60K before reaching the reaction temperature. The fast heating rate forexample may be between 150 to 200 K/h such as 180 K/h.

The reaction temperature depends on the EAM and can easily be determinedby thermogravimetry at a heating rate of e.g. 10 K/min.

The advantage of the heat treatment are the very precisely adjustableconditions so that side reactions can be avoided.

The heat treatment leads to crystalline coated LiEAMs.

Since Li₂C₂ is a strong reductant care has to be taken that anintercalation takes place and not a reduction. As already indicatedabove, undesired side reactions have to be avoided by careful control ofthe reaction conditions. Such an undesired side reaction is e.g. shownin equation 4:

2 MnO₂+Li₂C₂

2 MnO+Li₂O₂+C

From the coated particulate materials described herein electrodes can beprepared by mixing the coated LiEAM with an optionally electronicallyconducting binder, optionally in particulate form and optionally in thepresence of conductive additives like conductive carbon. The binding ofthe particulate coated LiEAM can be performed in a solvent followed bydrying.

Suitable binders are polyvinylidene fluoride (PVDF),poly(3,4-ethylenedioxythiophene)(PEDOT),1-cyclohexyl-3-(2-morpholinoethyl)carbodiimidemetho-p-toluenesulfonate or1-cyclohexyl-3-(2-morpholinoethyl)carbodiimide methyl-p-toluenesulfonate(CMC), polytetrafluoroethylene (PTFE), fluoro polymer rubber (FKS),styrene-butadiene rubber (SBR), polyacrylnitrile(PAN), polyurethane,polyacrylic acid, polyamide, polyacrylate, and polyvinylether.

Suitable conductive carbons are SuperP® or Super P Li® Carbon(obtainable from TIMCAL) or nanofibers or nanotubes.

Suitable solvents are a mixture of aprotic polar and aprotic apolarsolvents like THF/Toluene 4:1.

Dependent on the thermostability drying is preferably either performedat temperatures well above 100° C. like 180° C. under air, or attemperatures below 100° C. like 80° C. under vacuum.

Such electrodes can be used together with any suitable anode, and anelectrolyte like LiPF₆ or Li(C₂F₅)₃PF₃ (e.g. 1M in ethylene carbonate :dimethyl carbonate 1:1 (w/w))

The advantages of the new methods and the therewith produced coatedLiEAM are the enhanced purity due to the specific reactants. Inaddition, most of the carbon coating methods are performed via pyrolysisunder reducing conditions in order to avoid combustion instead ofpyrolysis. Therefore, it is impossible to coat numerous cathodematerials which are in a high oxidation state with these methods. Aseparate reduction/coating will reduce the oxidation state and thereforemake the EAM unuseable for cathodes.

In case of the one step method disclosed in U.S. Pat. No. 6,962,666 oneadvantage of the present method is also that due to the inventivereactions no pyrolysis takes place. Another advantage is the enhancedpurity and reproducibility due to the use of metallated reductants.

In one embodiment these reductants may be free from oxygen andoptionally free from oxygen and hydrogen which may result in betterdefined coatings and insertion/intercalation products.

The method of the invention is a surface contact reaction. Thus, due tothe specific starting materials and reaction conditions according to theinvention only the EAM is coated. Possible non-EAM side-products, e.g.impurities from EAM production, can be found during the coating reaction(e.g. optically due to having a colour different from black) andseparated from the product if desired. Furthermore the atom economy ofthe reaction is 100% or at least close to 100%, i.e. no metal or surfacecoating atom is wasted during the reaction. Compared to a pyrolysismethod the method of the invention is a very environment friendlyreaction due to the lower energy consumption and the about 100% atomeconomy. Especially if oxygen free reductants are used, no wastemanagement of the exhaust (CO, NO_(x)) is needed.

Another advantage of the method of the invention is that no solvent isneeded in the inventive coating reaction although in some cases use of asolvent might be useful.

The methods of the present invention lead to a predictable conversion ofthe coating precursor to the desired coating and predictable Li ionsinsertion since the reactions are stoichiometric. The invention alsoprovides reactions that can be performed at low temperature andtherefore are also suitable for coating temperature sensitive EAMs.

Contrary thereto the pyrolysis reaction of carboxylic acid salts will,dependent on the conditions and a specific EAM, in general lead todifferent compounds and to less defined coatings.

A further advantage of the inventive methods is that they can be used toproduce a variety of conductive non carbonaceous coatings.

BRIEF DESCRIPTION OF THE DRAWINGS

The invention will be better understood and objects other than those setforth above will become apparent when consideration is given to thefollowing detailed description thereof. Such description makes referenceto the annexed drawings, that show:

FIG. 1: X-Ray Powder Diffraction of the synthesized Li_(0.3)V₂O₅compared to the theoretical pattern.

FIG. 2: TEM-picture of Li_(0.3)V₂O₅ with carbon coating. The inter planedistance corresponds to the a-lattice parameter of Li_(0.3)V₂O₅.

FIG. 3: EDX-analysis of Li_(0.3)V₂O₅ with carbon coating (EDX=EnergyDispersive X-ray Analysis).

FIG. 4: Potential vs. specific charge for the Li_(0.3)V₂O₅ electrode.

FIG. 5: X-Ray Powder Diffraction of the synthesized LiV₂O₅ compared tothe theoretical pattern.

FIG. 6: Thermogravimetry of the reaction of Li₂C₂ with V₂O₅.

FIG. 7: Potential vs. specific charge for the LiV₂O₅ electrode.

FIG. 8: X-Ray Powder Diffraction of LiFePO₄ synthesized via heattreatment (450° C.) compared to the theoretical pattern.

FIG. 9: Potential vs. specific charge for the via heat treatmentsynthesized LiFePO₄ electrode.

FIG. 10: TEM-bright field picture of LiFePO₄ with carbon coating.

FIG. 11: Indexed Fourier Transformation of FIG. 9.

FIG. 12: X-Ray Powder Diffraction of LiV₂O₅ synthesized via ball millingcompared to the theoretical pattern.

FIG. 13: Potential vs. specific charge for the via ball millingsynthesized LiV₂O₅ electrode.

FIG. 14: TEM-bright field picture of Li_(0.3)MoO₃ with carbon coating

FIG. 15: Thermogravimetry of the reaction of Li₂C₂ with MoO₃via ballmilling.

FIG. 16: Potential vs. specific charge for the via ball millingsynthesized Li₀₃MoO₃ electrode.

FIG. 17: X-Ray Powder Diffraction of LiH₂V₃O₈ synthesized via ballmilling.

FIG. 18: Potential vs. specific charge for the via ball millingsynthesized LiH₂V₃O₈ electrode.

MODES FOR CARRYING OUT THE INVENTION Analytical and InvestigationMethods: Electrochemical Measurements:

Galvanostatic measurements were monitored by Astrol, a program fromAstrol Electronic AG. A potentiostat (BAT-SMAL, battery cycler) wasconnected using a serial cable to a personal computer (running WindowsXP) via a serial/analog converter. The composition of all electrodes was73% active material, 15% Super P® Carbon (obtainable from TIMCAL) and 2%polyvinylidene fluoride (PVDF). The materials were mixed in aTHF/Toluene 4:1 mixture. Finally the electrodes were dried at 180° C.under air. The only exception was the LiFePO₄ electrode that was driedat 80° C. under vacuum. The measurements were done with fixed currentsof 50 A/kg.

The electrolyte was LP30 (obtainable from Merck Chemicals), 1.4 mol/LLiPF₆ in ethylene carbonate/dimethyl carbonate 1/1 by weight. and thecounter electrode was a disk of metallic lithium with a diameter of 13mm and 0.5 mm thickness.

Differential— and Thermogravimetry:

The measurements were performed with a Netzsch STA 409 using corundumcrucibles using a heating rate of 10 K/min. The reference powder wascorundum, too. The measurements show (see FIGS. 6 and 15) that there isno significant mass loss below the reaction temperature of 600° C. forV₂O₅ and 400° C. for MoO₃. Thus the reactions are completely proceedingto the lithiated oxidants_(reduced) and carbon.

Powder Diffractometry:

The measurements were performed with a STOE STADI P2 diffractometer intransmission mode with germanium monochromator, CU_(ka1)=1.54056 A

Electron Microscopy:

Electron microscopy was performed in a Tecnai F30 microscope(manufactured by FEI) with a field emission gun (FEG), V_(acc)=300 kV,and C_(s)=1.2 mm

Experimental Part: Commercial Reactants and Electrolytes:

-   -   Lithium granule 99.9%, Aldrich    -   Graphite powder natural microcrystal grade, APS 2-15 micron,        99.9995%, Alfa Aesar    -   V₂O₅, 99.2%, Alfa Aesar    -   FeCl₃ anhydrous purum, Fluka    -   H₃PO₄ ortho-phosphric acid 85%, Merck    -   MoO₃ 99.5%, Sigma Aldrich    -   LiMn₂O₄, Merck    -   PVDF averabe Mw˜534,000 by GPC, Sigma Aldrich    -   LP30; 1M LiPF6 in ethylene carbonate : dimethyl carbonate 1:1        (w/w), Merck    -   LF30; 1M Li(C2F5)3PF3 in ethylene carbonate:dimethyl carbonate        1:1 (w/w), Merck, highly stable

Synthesized Materials [Source or Description of Method]: Oxidants:

-   -   FePO4 [C. Delacourt, Solid State Ionics, 173, 113-118, 2004]    -   MnO2 [Asulab]    -   NbNO [Nesper, R., Wang X.-J., EP 2 378 596 A1]    -   Glasses of V205 and Mo03 [Sakurei et al. U.S. Pat. No.        4,675,260]

Metallated Reductants:

-   -   Li₂C₂ [Armbruster, Dissertation (thesis), ETH Zurich No. 17553,        2008]    -   LiNaC₂ [R. Nesper, Habilitationsschrift, Stuttgart, 1998]    -   LiKC₂ [R. Nesper, Habilitationsschrift, Stuttgart, 1998]    -   Li₂NCN [Sokolov, Trudy po Khimi/Khimicheskoi Tekhnologii (2),        18-19, 1973]    -   Li₃BN₂ [Yamane, Journal of Solid State Chemistry 71(1), 1-11,        1987]

Heat Treatment: EXAMPLE 1 FIGS. 1 to 4:

1.5 Li₂C₂+10 V₂O₅→10 Li_(0.3)V₂O₅+3 C_(surface)

1.8 g (10 mmol) V₂O₅ and 0.0569 g (1.5 mmol) Li₂C₂ were mixed in amortar. Then the mixture was heated to 600° C. using a heating ramp of180° C./h and kept at 600° C. for 0.5 hours.

EXAMPLE 2 FIGS. 5 to 7:

5 Li₂C₂+10 V₂O₅→10 LiV₂O₅+10 C_(surface)

1.8 g (10 mmol) V₂O₅ and 0.1895 g (5 mmol) Li₂C₂ were mixed in a mortar.Then the mixture was heated to 600° C. using a heating ramp of 180° C./hand kept at 600° C. for 0.5 hours.

EXAMPLE 3 FIGS. 8 to 11:

3 Li₂C₂+6 FePO₄→6 LiFePO₄+6 C_(surface)

0.905 g (6 mmol) FePO₄ and 0.114 g (3 mmol) Li₂C₂ were mixed in amortar. Then the mixture was heated to 450° C. using a heating ramp of180° C./h and kept at 450° C. for 2 hours.

Ball Milling:

The starting materials indicated below were premixed in a mortar beforereacted in a Fritsch Pulverisette 6 with 400 rpm for 0.5 hours and at aratio between the weight of the balls and the weight of the sample of1:5.

EXAMPLE 4 FIGS. 12 and 13:

5 Li₂C₂+10 V₂O₅→10 LiV₂O₅+10 C_(surface)

1.8 g (10 mmol) V₂O₅ and 0.1895 g (5 mmol) Li₂C₂ were premixed in amortar. Then the mixture was reacted in a Fritsch Pulverisette 6 with400 rpm for 0.5 hours.

EXAMPLE 5 FIGS. 14 to 16:

1.5 Li₂C₂+10 MoO₃→10 Li_(0.3)MoO₃+3 C_(surface)

1.4394 g (10 mmol) MoO₃ and 0.0569 g (1.5 mmol) Li₂C₂ were premixed in amortar. Then the mixture was reacted in a Fritsch Pulverisette 6 with400 rpm for 0.5 hours.

EXAMPLE 6 FIGS. 17 and 181:

5 Li₂C₂+10 H₂V₃O₈→10 LiH₂V₃O₈+10 C_(surface)

2.8284 g (10 mmol) H₂V₃O₈ and 0.1895 g (5 mmol) Li₂C₂ were premixed in amortar. Then the mixture was reacted in a Fritsch Pulverisette 6 with400 rpm for 0.5 hours.

EXAMPLE 7 Electrode Preparation

From the coated particulate materials described above electrodes wereprepared by mixing 73% coated LiEAM 15% Super P® Carbon (obtainable fromTIMCAL) and 2% polyvinylidene fluoride (PVDF) in a THF/Toluene 4:1mixture and then drying at 180° C. under air, except for the LiFePO₄electrode that was dried at 80° C. under vacuum.

Analytical data and electrochemical behaviour is shown in the Figures asindicated to each example.

While there are shown and described presently preferred embodiments ofthe invention, it is to be distinctly understood that the invention isnot limited thereto but may be otherwise variously embodied andpracticed within the scope of the following claims.

1-11. (canceled)
 12. A coated at least partially metallated particulateelectroactive material that is crystalline or amorphous, obtained by aprocess comprising: premixing an oxidant electroactive material with ametallated reductant, followed by chemically reacting the oxidantelectroactive material with the metallated reductant, wherein: themetallated reductant is a coating precursor comprising an alkali metal,an alkaline earth metal, or both, the chemically reacting is performedunder a condition allowing reduction and metallation of the oxidantelectroactive material via insertion or intercalation of the alkalimetal and/or the alkaline earth metal and coating of the metallatedelectroactive material with a coating formed from the metallatedreductant, and wherein the coating formed from the metallated reductantcomprises at least one selected from the group consisting of: boronnitride formed from Li₃BN₂; carbon nitride formed from Li₂CN₂; carbonboride formed from Li₄BCB; carbon boron nitride formed from a lithiumpyrazine precursor; polymeric sulfur nitride formed from Li₉NS₃; andpolyacetylene formed from LiHC₂.
 13. An electrode comprising: the coatedat least partially metallated particulate electroactive material ofclaim 12, an optionally electronically conducting binder, optionally inparticulate form, and optionally a conductive additive.
 14. A method forproducing an electrode comprising the coated at least partiallylithiated particulate electroactive material of claim 12, the methodcomprising mixing the coated particulate material with an optionallyelectronically conducting binder, optionally in particulate form andoptionally in the presence of a conductive additive in an aproticsolvent followed by drying.
 15. A battery comprising: an electrode ofclaim 13 as cathode, an anode, and an electrolyte.
 16. The coated atleast partially metallated particulate electroactive material of claim12, wherein the condition comprises applying energy in at least one formselected from the group consisting of heat energy, tribological energy,ultrasonic energy, and microwave energy.
 17. The coated at leastpartially metallated particulate electroactive material of claim 12,wherein the metallated reductant comprises an alkali metal comprisinglithium and optionally sodium and/or potassium.
 18. The coated at leastpartially metallated particulate electroactive material of claim 12,wherein the reductant of the metallated reductant is oxygen free. 19.The coated at least partially metallated particulate electroactivematerial of claim
 12. wherein the oxidant of the oxidant electroactivematerial is selected from the group consisting of a transition metaloxide, a hydrated transition metal oxide, a transition metal oxynitride,a transition metal phosphate, a transition metal oxide glass, S, Se, andSi.
 20. The coated at least partially metallated particulateelectroactive material of claim
 19. wherein the oxidant of the oxidantelectroactive material is in the form of microparticles or nanoparticleshaving an average particle size below 10 μm, and wherein the metallatedreductant is in the form of microparticles with an average particle sizeof less than 10 μm.
 21. The coated at least partially metallatedparticulate electroactive material of claim 12, wherein the coating hasan average thickness of 0.5 nm to 30 nm.
 22. The coated at leastpartially metallated particulate electroactive material of claim 12,wherein the condition allowing reduction and metallation of the oxidantelectroactive material and coating deposition comprises applyingtribological energy by ball milling at a rotation speed of 200 to 1500rpm for 15 to 45 minutes, wherein a ratio between the weight of theballs and the weight of the sample is in the range from 6:1 to 4:1. 23.The coated at least partially metallated particulate electroactivematerial of claim 12, wherein the condition allowing reduction andmetallation of the oxidant electroactive material and coating depositioncomprises a heat treatment with a heating profile providing a slowheating rate of between 50 to 70 K/h for about at least the last hourbefore reaching the reaction temperature.
 24. The coated at leastpartially metallated particulate electroactive material of claim 23,wherein the heating profile comprises a fast heating rate of 180 K/huntil about 60 K below the reaction temperature, followed by a slowheating rate of about 60 K/h.
 25. The coated at least partiallymetallated particulate electroactive material of claim 12, wherein thecoating formed from the metallated reductant comprises boron nitrideformed from Li₃BN₂.
 26. The coated at least partially metallatedparticulate electroactive material of claim 12, wherein the coatingformed from the metallated reductant comprises carbon nitride formedfrom Li₂CN₂.
 27. The coated at least partially metallated particulateelectroactive material of claim 12, wherein the coating formed from themetallated reductant comprises carbon boride formed from Li₄BCB.
 28. Thecoated at least partially metallated particulate electroactive materialof claim 12, wherein the coating formed from the metallated reductantcomprises carbon boron nitride formed from a lithium pyrazine precursor.29. The coated at least partially metallated particulate electroactivematerial of claim 12, wherein the coating formed from the metallatedreductant comprises polymeric sulfur nitride formed from Li₉NS₃.
 30. Thecoated at least partially metallated particulate electroactive materialof claim 12, wherein the coating formed from the metallated reductantcomprises polyacetylene formed from LiHC₂.